CN1329549C - Heating technology for refining TiAl alloy ingot microscopic texture - Google Patents
Heating technology for refining TiAl alloy ingot microscopic texture Download PDFInfo
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- CN1329549C CN1329549C CNB2005100867262A CN200510086726A CN1329549C CN 1329549 C CN1329549 C CN 1329549C CN B2005100867262 A CNB2005100867262 A CN B2005100867262A CN 200510086726 A CN200510086726 A CN 200510086726A CN 1329549 C CN1329549 C CN 1329549C
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 40
- 239000000956 alloy Substances 0.000 title claims abstract description 40
- 229910010038 TiAl Inorganic materials 0.000 title claims abstract description 34
- 238000010438 heat treatment Methods 0.000 title claims abstract description 11
- 238000007670 refining Methods 0.000 title claims abstract 3
- 238000005516 engineering process Methods 0.000 title description 12
- 238000005242 forging Methods 0.000 claims abstract description 38
- 150000003839 salts Chemical class 0.000 claims abstract description 31
- 238000000034 method Methods 0.000 claims abstract description 30
- 238000010791 quenching Methods 0.000 claims abstract description 28
- 230000000171 quenching effect Effects 0.000 claims abstract description 28
- 230000008569 process Effects 0.000 claims abstract description 17
- 230000032683 aging Effects 0.000 claims abstract description 14
- 238000012545 processing Methods 0.000 claims abstract description 9
- 238000001816 cooling Methods 0.000 claims description 9
- 238000010275 isothermal forging Methods 0.000 claims description 4
- 238000005266 casting Methods 0.000 abstract description 17
- 239000010955 niobium Substances 0.000 abstract description 6
- 229910052758 niobium Inorganic materials 0.000 abstract description 5
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 abstract description 5
- 239000007769 metal material Substances 0.000 abstract description 2
- 239000012071 phase Substances 0.000 description 70
- 239000013078 crystal Substances 0.000 description 19
- 230000009466 transformation Effects 0.000 description 11
- 230000008859 change Effects 0.000 description 7
- 239000007787 solid Substances 0.000 description 6
- 238000007669 thermal treatment Methods 0.000 description 6
- 230000015572 biosynthetic process Effects 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 5
- 230000007704 transition Effects 0.000 description 5
- 238000000354 decomposition reaction Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000000465 moulding Methods 0.000 description 4
- 238000002791 soaking Methods 0.000 description 4
- 229910000601 superalloy Inorganic materials 0.000 description 4
- FAPWRFPIFSIZLT-UHFFFAOYSA-M Sodium chloride Chemical compound [Na+].[Cl-] FAPWRFPIFSIZLT-UHFFFAOYSA-M 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 238000009413 insulation Methods 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 239000003963 antioxidant agent Substances 0.000 description 2
- 230000003078 antioxidant effect Effects 0.000 description 2
- 235000006708 antioxidants Nutrition 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000011160 research Methods 0.000 description 2
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 229910004349 Ti-Al Inorganic materials 0.000 description 1
- 229910004692 Ti—Al Inorganic materials 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000012797 qualification Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000012827 research and development Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000011780 sodium chloride Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001256 stainless steel alloy Inorganic materials 0.000 description 1
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Abstract
一种细化TiAl合金铸锭显微组织的热加工工艺，属于金属材料领域，适用于Al含量为45at.%到48at.%TiAl合金和铌含量范围为6at.%到8at.%的高铌TiAl合金。本发明具体来讲，就是对经过浇注或凝壳或提拉成型的TiAl合金铸锭，首先进行一次或多次盐浴淬火+时效的热处理工艺，然后再进行一次中等变形量的高温锻造工艺使原始粗大的铸造组织得到有效地细化，而且，显微组织的均匀性也较高，其室温塑性(延伸率)可以达到并且可以稳定在2%以上。
A thermal processing process for refining the microstructure of TiAl alloy ingots, which belongs to the field of metal materials, and is suitable for TiAl alloys with an Al content of 45 at.% to 48 at.% and high niobium with a niobium content ranging from 6 at.% to 8 at.%. TiAl alloy. Specifically speaking, the present invention is to carry out one or more heat treatment processes of salt bath quenching + aging for the TiAl alloy ingots that have been cast, solidified, or pulled, and then perform a high-temperature forging process with a medium deformation amount. The original coarse casting structure is effectively refined, and the uniformity of the microstructure is also high, and its room temperature plasticity (elongation) can reach and be stable at more than 2%.
Description
Technical field
The invention belongs to metal material field, particularly a kind of heat processing technique of thinning TiAl alloy cast ingot microstructure.
Background technology
The TiAl alloy is a kind of novel high-temperature structural material, has advantages such as density is low, high-temperature behavior is good, is considered to have aircraft engine of future generation one of structured material of competition potential.Compare with the most sophisticated materials for aeroengines-nickel base superalloy at present, the density of TiAl alloy has only 3.7～3.9g/cm
3, not enough nickel base superalloy density (7.9～9.5g/cm
3) half, this is for the aircraft engine parts, its superiority is self-evident, and, the creeping limit of TiAl alloy is 750 ℃～950 ℃, the anti-oxidant limit is 800 ℃～950 ℃, near 870 ℃～1090 ℃ of 800 ℃～1090 ℃ of the creeping limits of nickel base superalloy and the anti-oxidant limit.Yet its lower temperature-room type plasticity, fracture toughness property and high crack growth rate have seriously hindered it and have entered the process of practicability.Solve an above-mentioned difficult problem, the problem of temperature-room type plasticity difference especially becomes the focus and the key problem of the research and development of TiAl alloy.
At the problem of TiAl alloy temperature-room type plasticity difference, carried out and carried out a large amount of research both at home and abroad.From present present situation, the reason of temperature-room type plasticity difference mainly contains: the order of atomic arrangement and interatomic covalent bonds characteristic in the TiAl alloy; Less and the deformation mechanism complexity of microdeformation mode; Coarse microstructure and interface bond strength are low; Or the like.For this reason, improve its temperature-room type plasticity, become several main research directions at present by alloying, change material preparation and methods such as moulding process, the hot-work of change material and thermal treatment process.Result of study shows that the microstructure of TiAl alloy affects its room-temperature mechanical property significantly, and tiny, uniform microstructure can make alloy in the higher mechanical behavior under high temperature of maintenance, obtains higher room-temperature mechanical property.Further result of study shows, by thermal treatment, or repeatedly forges by high temperature, can change the structural state of TiAl alloy cast ingot effectively, makes its microstructure obtain refinement effectively.The heat treating method of having reported mainly contains cycle heat treatment, two warm processing etc., it mainly acts on is to obtain more even, tiny microstructure, and cost is lower, but shortcoming is to eliminate dentrite and some casting flaw in the microstructure effectively, as loose, cavity etc.And high temperature repeatedly forges and mainly contains isothermal forging, canned forging etc., it mainly acts on is to access more tiny microstructure, and can eliminate dentrite and some casting flaw effectively, but shortcoming is a Deformation structure extremely inhomogeneous (owing to existing the distortion dead band), therefore causes the less stable of performance.Though can improve the homogeneity of tissue by forging deformation repeatedly, its cost is improved, lumber recovery reduces, and, repeatedly forge and cause the spindle cracking easily.When organizing behind the high temperature forging further carried out the homogeneous microstructure processing again, promptly utilize thermal treatment to come homogenizing to forge when organizing again, though the homogeneity of structure of forging deformation is greatly improved, but meanwhile, the small grains that forging deformation forms will be grown up, and counter its temperature-room type plasticity that makes significantly reduces, near the level of directly heat-treating, the advantage of high temperature forging distortion is cut down, therefore, after the forging again heat-treating process be subjected to suspection.
Summary of the invention
The present invention seeks to solve cycle heat treatment or two warm processing and can not eliminate in the microstructure casting flaw problems such as dentrite and loose, cavity effectively, and solve isothermal forging, the Deformation structure that brings inhomogeneous (existing the distortion dead band) is made in the contour warm forging of canned forging, thereby cause the poor stability of performance, spindle cracking problem occurs easily.
A kind of heat processing technique of thinning TiAl alloy cast ingot microstructure, it is characterized in that before high temperature forging, carry out the thermal treatment of one or multi-channel salt bath quenching+timeliness earlier, and then carry out a high temperature forging technology and can realize the refinement and the homogenizing of cast structure.This salt bath quenching+aging technique is the microstructure of thinning TiAl alloy cast ingot effectively not only, simultaneously, also will have influence on follow-up high temperature forging technology, a little crackle of leaving over when making the purpose of follow-up high temperature forging technology change into further elimination dendritic segregation, casting flaw and salt bath quenching etc., rather than for further thinning microstructure, so, can not cause the even and spindle cracking phenomena of the tissue odds that causes greatly because of deflection.By this technology, the original thick cast structure of refinement effectively not only, and the tissue defects of TiAl alloy cast ingot and the defectives such as inhomogeneity of structure behind the high temperature forging are greatly improved, thereby have improved TiAl alloy cast ingot temperature-room type plasticity and stability thereof.Simultaneously, the deflection when this technology has reduced the number of times of high temperature forging distortion and reduced the high temperature forging distortion makes that TiAl alloy cast ingot rimose risk significantly reduces in the cost of high temperature forging distortion and the forging deformation process.Through above-mentioned technology, the mean diameter of its crystal grain is 50 μ m, and corresponding fiducial probability is 90%, and temperature-room type plasticity (unit elongation) can reach and can be stabilized in more than 2%.
At first salt bath quenching+the aging technique that carries out is by original structure being heated to eutectoid temperature T
αMore than the temperature, make it change the α phase fully into, then, by salt bath quenching, change α into unsettled block γ phase (massively transformed gamma) mutually fully, more then, by ageing treatment, make unsettled block γ that branch take place mutually and parse the α phase.Because α has only a kind of (0001) solid matter face mutually, and γ has four kinds of { 111} solid matter faces mutually, so, when the block γ phase time of the mutually fast cold formation of α, be α → γ, α phase crystal grain can only by its unique solid matter face be transformed into a position to γ phase crystal grain, and when unsettled block γ phase timeliness is decomposed, be γ → α, γ phase crystal grain can by its 4 solid matter faces be transformed into 4 positions to α phase crystal grain.Like this, original thick cast structure just can obtain refinement effectively by the transformation mutually of α γ, and refinement original structure can make that the follow-up high temperature forging deformation technique that carries out becomes easily.Salt bath quenching+aging technique also can replace with cycle heat treatment or two warm treatment process, carries out high temperature forging then one time.With respect to cycle heat treatment technology, i.e. oil quenching or shrend by repeatedly realizes the transformation of α phase → block γ phase and the decomposition of block γ phase, the quenching temperature of salt bath quenching is higher, more than TiAl alloy Cold Brittleness Transition Temperature, thereby can avoid quenching crack effectively; Two relatively warm treatment process are promptly at T
αAnd T
ePhase transformation repeatedly mutually comes thinning microstructure with lath γ mutually by α between the temperature, and salt bath quenching+aging technique can reduce heat treatment time effectively; And relatively-high temperature forging process repeatedly, the follow-up high temperature forging among the present invention, not only being out of shape number of times reduces, and deflection also reduces greatly, and the cost of forging deformation and success ratio all can be greatly improved, and demonstrates tangible positively effect.
The present invention at the composition of TiAl alloy, one is high content of niobium TiAl alloy, the content of niobium scope is 6at.%～8at.%, another is the TiAl alloy of common constituent, the aluminium content range is 45at.%～48at.%.When they when being frozen into the room temperature ingot casting by high temperature fluent metal, following phase transformation (seeing accompanying drawing 1) has taken place: during by liquid phase cools, at first form solid phase α, alpha-crystal will be according to qualifications along its C axle growth, thereby form tangible columanar structure.In process of cooling subsequently, alloy enters α+γ two-phase region, will separate out lath-shaped γ phase from the α column crystal.Keep definite orientation relationship between γ phase and the α phase:
(0001)α//{111}γ，<1120>α//[111]γ
When continuing cooling, eutectoid reaction will take place and form α in α mutually
2The full lath tissue of+γ.α
2Ordering transition takes place and forms in α mutually mutually.Because fixed orientation relationship between γ phase and the α phase is so all γ phase laths will present ingot structure and typically organize anisotropy perpendicular to the direction of growth of α phase column crystal.When speed of cooling increases, will separate out the γ phase of Widmannstatten structure (Widmanstatten) or featheriness tissue (feathery) from α mutually, and the γ phase of massive texture (massive).The γ of massive texture is unstable mutually, branch can take place under heating state parse the α phase.
When ingot casting carries out salt bath quenching, be about to ingot casting and be heated to T
αWhen temperature is above, as-cast structure originally, i.e. (α
2+ γ) full lath tissue is converted into single-phase α and organizes.Because the α in the ingot casting of this composition
2Phase content is less, and therefore, the form of α phase will directly be subjected to the influence of γ phase lath.Because this moment, the formation of α phase was a kind of nucleation process again, the new α phase crystal grain that forms is more tiny, and, because the temperature of this moment is higher, and does not have the second phase pinning, so, if soaking time is longer, the α phase crystal grain of new formation is grown up fast.Two temperature heat-treating methods, the solid-state phase changes when utilizing the phase co-conversion between lath γ phase and the α phase are come the refinement ingot structure.But method of the present invention is with newly formation, less α are cooled fast to eutectoid temperature (T mutually
e) below, i.e. γ+below the α two-phase region, make α be transformed into block γ phase mutually, rather than lath-shaped γ phase.The block γ phase constitution that form this moment will be significantly less than lath-shaped γ phase constitution.Lath-shaped γ at room temperature is a kind of stable structure phase mutually, and block γ at room temperature is a kind of unsettled structure phase mutually, at comparatively high temps (T
αAnd T
eBetween the temperature) during timeliness, block γ will decompose mutually, separate out the α phase.Owing to be at T
αSeparate out below the temperature, so the α that separate out this moment is difficult to grow up mutually, and, owing to separate out the α phase time mutually from γ, γ phase crystal grain can by its 4 solid matter faces separate out 4 positions to α phase crystal grain, and do not resemble the block γ phase time of the mutually fast cold formation of α, α phase crystal grain can only by its unique solid matter face be transformed into a position to γ phase crystal grain such, so, the α phase crystal grain that timeliness is separated out will original tiny block γ phase crystal grain be refined as again 4 positions to the zone.If organizing of starting ingot is comparatively thick, can be by twice or the repeatedly in addition refinement of method of salt bath quenching+timeliness.
Through above-mentioned processing, original thick ingot structure will obtain refinement effectively, but the casting flaw of this moment, and because the fast cold defective of bringing into of salt bath quenching will be present in the heat treatment on microstructure, therefore, also need a high temperature forging distortion, further improve and complete tissue.The temperature range of forging deformation is 1230 ℃～1250 ℃, is in γ+α two-phase region, thus this moment do not organize and can obviously grow up.Owing to the refinement of organizing of this moment, therefore, the number of times and the deflection of needed high temperature forging distortion will reduce and reduce.Like this, the homogeneity of fine tissue will can not be subjected to tangible influence, and the high temperature forging distortion of appropriateness also helps the further refinement and the homogenizing of tissue, guarantees the stability of its room-temperature property.
The advantage of salt bath quenching+timeliness, be exactly that it is not as two warm treatment process, by the long time (being generally 18～48 hours), utilize the transformation mutually between lath γ phase and the α phase to come the refinement ingot structure, also not as cycle heat treatment, realize that by oil cooling or water-cooled repeatedly α arrives the transformation of block γ phase and the decomposition of block γ phase mutually, the easy quenching crack that causes like that, but realize that by salt bath quenching α arrives the decomposition of the transformation of block γ phase and block subsequently γ phase mutually.Because the salt temperature scope at 800 ℃～820 ℃, is higher than the Cold Brittleness Transition Temperature (being generally 500 ℃～700 ℃) of TiAl alloy, so the TiAl alloy during salt bath quenching at this moment still is in plastic state, salt bath quenching can not cause quenching crack.And, will be near T
αThe above α of temperature is as cold as T mutually soon
eWhen eutectoid temperature is following, promptly about below 1100 ℃ the time, can realize that fully α arrives the transformation of block γ phase mutually, it is simple to make that the step that realizes this operation becomes, control easily.Aging time after the salt bath quenching was generally 1～2 hour, therefore, its cost was reduced greatly, and economic worth is considerable.
This kind technology not only is suitable for the TiAl alloy cast ingot of common constituent, and (the Al content range is 45at.%～48at.%), and (the Nb content range is 6at.%～8at.%) to be suitable for the TiAl alloy cast ingot of high content of niobium; Not only be suitable for the TiAl alloy cast ingot of common induction melting moulding, and be suitable for the TiAl alloy cast ingot of consumable smelting and ionic fluid melting moulding.
Description of drawings
Fig. 1 is the Ti-Al binary phase diagram
Embodiment
To through cast or scull or lift the TiAl alloy cast ingot of moulding, carry out salt bath quenching+ageing treatment, and the distortion of high temperature forging subsequently, its embodiment is as follows:
(1) the TiAl alloy cast ingot is heated to more than the T α temperature about 10 ℃～15 ℃, the insulation certain hour.The length of this soaking time is relevant with the gauge of ingot casting, determines the time of insulation according to 1 mm/min.For example, 100 millimeters cylinder ingot casting, then soaking time is 50 minutes.Usually, soaking time is to be no more than 60 minutes for good.
(2) above-mentioned ingot casting is quenched fast in the salt bath, ingot casting is transferred to time the salt bath at 5～10 seconds from process furnace, with the requirement greater than 100 ℃/second of the speed of cooling that satisfies salt bath quenching subsequently, makes α can change block γ phase fully into mutually.Ingot casting is incubated 10～20 minutes in salt bath.The working temperature of salt bath is 800 ℃～820 ℃, and the composition proportion of salt bath is (80%～82%) BaCl
2+ (18%～20%) NaCl (wt.%).
(3) according to the size of ingot casting original grain, can be according to above-mentioned technology, circulation is carried out 2～3 times, is converted into block γ tissue fully to guarantee α crystal grain thick in the original structure.
(4) at T
αTemperature is carried out ageing treatment (about 1300 ℃～1320 ℃) for following 20 ℃～40 ℃.Aging time is according to the difference of the composition proportion of virgin alloy and difference was generally 1～2 hour.Stove is as cold as 1250 ℃ more afterwards, is incubated 4 hours, and air cooling obtains tiny nearly complete lamellar structure to room temperature.
(5) in 1230 ℃～1250 ℃ temperature ranges, carry out canned forging or isothermal forging.The forging deformation amount is not more than 50%, and rate of deformation is 1 * 10
-2～1 * 10
-3/ second.Behind the forging deformation, the air furnace stove of putting into 900 ℃ at once is chilled to room temperature, obtains tiny bifurcation tissue.
Nomenclature and chart
(1) nomenclature
At.%---atomic percent
Wt.%---weight percent
Salt bath quenching---workpiece is inserted the fused saline solution fast from high temperature
Oil quenching---workpiece is inserted the quenching oil fast from high temperature
Timeliness---insulation when workpiece is grown under a certain temperature is so that have second to separate out mutually.
α phase---hexagonal structure Ti phase
α
2---orderly body-centred structure Ti
3The Al phase
γ---orderly square structure TiAl phase
T
α---α begins to separate out the temperature (cooling) of γ phase mutually, or the γ phased soln is in the temperature (intensification) of α in mutually.
T
e---the temperature (α → α of eutectoid transformation takes place
2+ γ)
Cold Brittleness Transition Temperature---alloy is changed into the transition temperature of brittle state by plastic state
Canned forging---with stainless steel or superalloy the ingot casting jacket is got up to heat and forged technology.Forging is at room temperature to carry out.
Isothermal forging---workpiece forges under constant temp
Two warm processing---refer in particular at T
αAnd T
eBetween the temperature, come a kind of thermal treatment process of refinement ingot structure by the transformation mutually between γ phase and the α phase.
Cycle heat treatment---refer in particular to by oil cooling or water-cooled repeatedly, utilize α to come a kind of thermal treatment process of refinement ingot structure to the decomposition of the transformation of block γ phase and block γ phase mutually.
Complete lamellar structure---all by α
2The microstructure that+γ synusia group forms
Nearly complete lamellar structure---by α
2+ γ synusia group and a small amount of microstructure that waits axle shape γ crystal grain to form
Bifurcation tissue---the α that waits axle shape γ crystal grain and about 50% by about 50%
2The microstructure that+γ synusia group forms
(2) T of several alloys
αTemperature
The T of several alloys of table 1
αTemperature
| Alloy | ?T αTransition temperature (℃) |
| ?Ti—46Al-2Cr-2Nb-1B | ?1320 |
| ?Ti-48Al-2Cr-2Nb-1B | ?1370 |
| ?Ti-48Al-2Cr-2Nb | ?1365 |
| ?Ti-46Al-4Nb-4Hf-0.1Si-1B | ?1360 |
Claims (1)
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|---|---|---|---|
| CNB2005100867262A CN1329549C (en) | 2005-10-26 | 2005-10-26 | Heating technology for refining TiAl alloy ingot microscopic texture |
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|---|---|---|---|
| CNB2005100867262A CN1329549C (en) | 2005-10-26 | 2005-10-26 | Heating technology for refining TiAl alloy ingot microscopic texture |
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| CN1752265A CN1752265A (en) | 2006-03-29 |
| CN1329549C true CN1329549C (en) | 2007-08-01 |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2936173B1 (en) * | 2008-09-22 | 2012-09-21 | Snecma | PROCESS FOR THE MANUFACTURE OF A TITANIUM PIECE WITH INITIAL FORGING IN THE BETA DOMAIN |
| CN103409711B (en) * | 2013-08-26 | 2015-09-09 | 中南大学 | A preparation method of TiAl-based alloy with fine full-layer lamellar structure |
| CN104588997B (en) * | 2015-01-20 | 2017-06-20 | 哈尔滨工业大学 | A kind of method that nearly isothermal die forging process prepares TiAl alloy component |
| CN105821470B (en) * | 2016-04-14 | 2018-09-25 | 南京理工大学 | A kind of dual structure TiAl alloy and preparation method thereof |
| CN105839039B (en) * | 2016-04-26 | 2017-08-25 | 哈尔滨工业大学 | A kind of preparation method of the TiAl alloy sheet material of uniform formation |
| CN106756688B (en) * | 2016-11-22 | 2018-11-27 | 北京科技大学 | A kind of deformation TiAl alloy structure property accuracy control method |
| CN110079753A (en) * | 2019-04-24 | 2019-08-02 | 江苏理工学院 | A kind of forging method for eliminating TiAl alloy remnants lamella |
| CN114657489B (en) * | 2022-03-16 | 2022-11-25 | 西北工业大学 | Double-temperature heat treatment process for uniform microstructure of titanium-aluminum alloy extruded rods |
| CN115522152B (en) * | 2022-11-07 | 2023-06-16 | 西北工业大学 | Method for simultaneously improving high-temperature plasticity of TiAl alloy |
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2005
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Non-Patent Citations (3)
| Title |
|---|
| 循环热处理过程中TiAl基合金细小全层片组织的形成 彭超群、舒畅、黄伯云，有色金属，第55卷第1期 2003 * |
| 热处理对TiAl基合金相变和显微组织的影响 彭超群、黄伯云、贺跃辉，材料科学与工艺，第10卷第3期 2002 * |
| 热处理对TiAl基合金相变和显微组织的影响 彭超群、黄伯云、贺跃辉，材料科学与工艺，第10卷第3期 2002;循环热处理过程中TiAl基合金细小全层片组织的形成 彭超群、舒畅、黄伯云，有色金属，第55卷第1期 2003 * |
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